Abstract: The achievement of hypereutectic Al-Si alloys with completely nodular eutectic Si has been studied. The procedure contained two steps: firstly, achieving hypereutectic directelectrolytic Al-Si alloys (HDEASA) with completely eutectic structure and secondly,spheroidizing eutectic Si upon soaking. HDEASAs with Si level in the range from 13.2 wt% to 17.6 wt% were made from directelectrolytic eutectic Al-Si alloy ingot and Al-50 wt% Si hardener. Ascast microstructure of HDEASA was composed of primary-free quasi-eutectic cells. In comparison with commercial alloys, the lower heating temperature of 505°C -515°C for 4-8 hrs was required to fully spheroidize Si crystal, either fine fibrous or even flaky in casting. Most of the spheres ranged in size from 1.0μm to 4.0μm. Many measurements were focused on the variety of Si phase size in eutectic cells against the distance from the center of the cells. The origin of granulation of primary-free quasi-eutectic Si crystal is associated with its thermodynamic structural instability, accompanied by crystallographic defects, related to the electrolytic process.

Hypereutectic Al-Si alloy offering excellent wear resistance, lower density and thermal expansion coefficient, and superior dimensional stability at high temperature is selected as the material for the fabrication of automotive componentsand other wear-resisting parts as the drive to reduce fuel consumption and CO2 emissions has recently become more intense. Its largescale application began in the late 1970s[1].Howeverthe appearance of coarse primary Si crystals seriously impairs its strength, toughness and machinability, limiting its usage in industry. Over several decades, many treatments have been focused on how to refine and modify the primary Si phase in hypereutectic alloys. They fall into three groups: chemical method, physical method and combined method. Chemical treatment is often used in practice, including the addition of an individual element or combination. In 1953 Mascre reported that the primary Si in hypereutectic alloys could be made dendritically or roughly spherical in chill casting by adding Na in the range of 0.05wt% to 0.1wt% to the melt[2]. In 1989 it was found that a combined Na-Sr treatment can result in a great number of fine spherical Si crystals[3]. However, the increase in porosity with Na-addition severely deteriorated the properties of the alloy. Trace addition of any elements such as: P [4,5], S[6], B[7], La[8],Ce[9], and RE[10-12] brings about refinement of primary Si in different degrees. Among these, P-addition significantly causes a reduction in the size of primary Si particles, increasing the number evenly distributed through the eutectic matrix. The combination of Si+P [13], RE+P[14], B+P[15] or Al-Ti-C[16] strongly enhances the refinement effect on primary Si induced by P-addition with modified eutectic Si. Recently it was found that adding a small amount of γ-Al2O3nano-particles simultaneously refined and modified the Si particles, and reduced the porosity in cast Al–20Si–4.5Cu, resulting in unusual ductility enhancement[17,18].But these chemical additions, either individually or complex, don’t lead the morphological change from multi-faceted primary Si into spheres. The physical method involves overheating[19-21], electromagnetic stirring[22,23] and electric current[24,25] which greatly refine the primary Si and modify its morphology.However, expensive equipment and complex operation restrict their usage in foundry. Quenching treatment achieved by chill casting and rapid cooling with melt spinning[26] comprise the powerful physical tool to reduce the size of primary Si. Note that those treatments are inapplicable in sand castings or for large castings. In recent years the combined methods have been developed. F.Y. Cao reported that superheating hypereutectic Al-Si alloy modified with the addition of P can reduce the size of primary Si from 145μm to 38μm, then after heat treatment at 535°C for 12hr the edges of primary Si become blunt, whereas the eutectic Si transforms to the spherical shape[27]. At the beginning of this century the author developed a combined process to nodulize the Si crystals, either eutectic or primary, in hypereutectic Al-Si alloy in two steps; firstly by adding the master alloy with several compositions (P, B, Ti and RE) to the melt, and then by heating the modified alloy at 510°C- 520°C for 8hr to granulate the eutectic Si aggregate and make the primary Si crystal smooth and round[28,29]. Achievement of a fully quasi-eutectic structure is another method to modify the primary Si phase. In the 1980s it was reported that the 3HA alloy, which contains up to 15wt% Si and 0.1wt% Sr exhibits a completely eutectic microstructure during directional solidification[30]. However, the microstructural benefit was offset by the appearance of porosity in the alloy. Recently M. Shamsuzzoha et al[31] reported that hypereutectic alloys having 14wt%-17wt% Si prepared by the addition of Ba in the range of 1wt%-4wt% induced a very fine eutectic structure with a very small amount of refined primary Si. It is of interest, as reported in our previous study [32],that direct electrolytic Al-Si alloy (DEASA) ingots having up to 12wt% Si solidify in a self-modified manner, accompanied by a large amount of Al-dendrite. Moreover, electrolytic hypereutectic Al-Si alloys with Si concentration up to 17wt% made from DEASA ingot provided a primary-free completely eutectic structure, even in a modified manner [33]. The most important event is that the eutectic Si precipitation in DEASA becomes small nodules after heating at a lower temperature of 505°C-515°C in a shorter time of 4-8 hrs [34] than in a Na-modified eutectic Al-Si alloy[35]. It would be expected that such a hypereutectic Al-Si alloy is capable of a spheroidizing Si phase at a lower temperature of near 510°Cfor a shorter heating time. If so, undoubtedly, it would represent a superior potential to challenge the increasing demand for lightweight alloy in automobile components in the near future and a new way of producing hypereutectic Al-Si alloy with completely smaller nodular Si offering high strength, toughness and wear-resistance.In this paper the aim focuses on the following:

•Observe the microstructural variety in hypereutectic Al-Si alloys heated at a lower temperature of 505°C-515°C.

•Study the effect of the Si level on the microstructural characteristics.

2. Experimental Procedure

Eutectic DEASA (EAl-12Si, Table 1) ingot of 10Kg and Al-50% Si master alloy along with other master alloy additions were used to make Al-Si alloys in the range of 11wt% to 18wt% Si in a 2 kg graphite crucible in an electric furnace which was heated to 850°C. The hardeners added were stirred into the melt. No modifier was added to the melt. After melting, homogenization of the molten alloy was held for 15 min., and then poured into a metallic mold, preheated to 250°C to form a casting of 40 x 50 x 120 mm3. Pouring temperature was about 740°C for all alloys tested. A chromel-alumelthermocouple of 0.1mm diameterwas put into the center of the casting and the temperature measurement was recorded by both a potentiometer and a digital potentiometer. The cooling rate during solidification was about 1.0°C/sec. DEASA ingot is made from Chinese bauxite [36].The chemical analyses of the alloys tested are listed in Table1.Note that the amount of modifying elements, e.g. Sr, Ca and others is less than the critical level required to modify the eutectic Si as reported in our previous studies [32,33].It is expected that the morphological characteristic in HDEASAs doesn’t associate with the trace elements.Specimens for microstructural observation were cut from the center of castings and heated at 505-515°C for 4-8 hrs in an electric furnace.Thesamples were polished in the conventional metallographic way and a series of image analysismeasurements related to the Si aggregate were conducted witha Quantiment Q920.

Table 1.Chemical Analysis of HDEASAs tested (wt%).

Alloy

Si

Mg

Cu

Mn

Ni

Fe

Ti

Sr

Ca

Zn

Remark

EAl-12Si*

11.76

0.60

1.27

0.39

0.10

0.26

0.10

<0.002

0.001

0.0070

DEASA ingot

EAl-13Si

13.20

0.42

0.84

0.27

0.05

0.27

0.03

0.0020

0.001

<0.015

D**+3wt%AS50***

EAl-14Si

14.20

0.52

0.85

0.28

<0.05

0.25

0.04

<0.0007

<0.001

0.0015

D+5wt%AS50

EAl-15Si

15.60

0.57

1.05

0.35

0.05

0.33

0.05

0.0017

0.001

0.0020

D+8wt%AS50

EAl-18Si

17.60

0.39

0.75

0.25

<0.05

0.35

0.04

<0.0006

<0.001

0.0017

D+12 wt%AS50

*E: electrolytic.**D: DEASA ingot.***AS50: Al-50wt% Si master alloy.

The parameters measured were: width b and length l, number of Si particles and the spacing between neighboring Si grains. The ratio of length to width, i.e. aspect ratio, of silicon grain is defined as its spheroidization rate. The contour of Si grain is, to a great degree, elliptical with long and short axes. Length and width are defined as the length of long and short axes, respectively. The volume of a Si grain is evaluated according to its length and width. To study the variety of Si sizes and morphologies in eutectic cells, a series of concentric circles were drawn in the photographs of several cells. The difference between radii of two neighboring circles was 10μm, and the widths and lengths of the Si grains in the spaces between two circles were measured.

As is well known, the eutectic arrest temperature, TE, in Al-Si alloy is related to the alloying elements such as Si, Mg, Cu, Mn, Ni, Fe and Zn [37,38]. In general the following equation (1) is used to estimate the change of TE in commercial alloys, where the total of Al% + Si% is high, near 99% [39,40].TE(°C) = 577－(12.5/ %Si) [4.43(% Mg) + 1.43(% Fe) + 1.93(% Cu) +1.7(% Zn) +3.0(% Mn)+4.0(% Ni)] (1)In present work the estimated eutectic arrest temperatures, TE, range from 569°C to 573°C, depending upon the composition of alloys tested. Thus the undercooling, △T, will be△T = TE - TE’ (2)Where TE’ is the measured eutectic temperature for a given alloy.

3. Results and Analysis

The procedure used to achieve a hypereutectic Al-Si alloy with completely nodular eutectic Si contains two steps. The first step is to obtain a quasi-eutectic structure in casting, and the second step is to granulate the eutectic Si grain by soaking at high temperature.

3.1. Achievement of Quasi-Eutectic Structure

Eutectic EAl-12Si alloy ingot of 10 kg with 100×70×600mm3 is an undercooled metal with excellentmicrostructural inheritance, displaying a hypoeutectic structure with a very fine self-modified eutectic structure upon remelting as shown in Figure 1[32]. That is related to adepressed eutectic arrest temperature of 557°C in freezing, corresponding to a highundercooling △T of 12°C estimated by equation (2), shifting the eutectic silicon content toward a higher level of 16 wt%[41-45]. In terms of the concept of eutectic shift a quasi-eutectic structure with Si levelsup to 16wt% can be obtained.

For achieving hypereutectic alloys a larger amount ofAl-50wt%Si master alloy is needed to add to the molten EAl-12Si ingot (Table 1), substantiallyincreasing the amount of unsolved Si particles acting as nuclei in the freezing of the alloys.Therefore a higher decrease in eutectic undercooling then appears, causing the considerablefading of self-structural inheritance [33]. With increase in the Si content from 11.7wt% (EAl-12Sialloy) to 13.2wt% (EAl-13Si), to 14.2wt% (EAl-14Si), and to 15.6wt%(EAl-15Si) the eutecticundercooling gradually drops down from 12°C to 11°C, to 9°C, and to 7°C, respectively, causing thealloys to grow into primary free quasi-eutectic structures in the different modified manner (Figure2-4). As Si level increases, the average widths and lengths of the siliconcrystals grow larger, producing higher aspect ratios (Fig.5), implying that the microstructural fading gradually becomes stronger.

Fig. 2. As-cast microstructure of hypereutectic EAl-13Si alloy, which is composed of the quasi-eutectic structure. The eutectic cell is undistinguishable. Optical.

Fig.3. As-cast micrograph of hypereutectic EAl-14Si alloy, showing the quasi-eutectic structure. Eutectic cell circled by dotted line grows as a nodule. ⅠandⅡarrow indicate the cells, of which width and length are measured (Fig.6)Optical.

Fig.4.As-cast microstructure of EAl-15Si alloy is composed of quasi-eutectic,which is subjected to considerable fading in self-modified structure. The cell boundary is unnoticeable. Optical.

All the microstructures (Figure2-4)are composed of many cellular eutectics. In the center ofeach cell the Si crystal exhibits a modified morphology, of which both width and length are verysmall with aspect ratios in the range of 2-3 (Figure 6). With an increase in distance from the center of the cell bothdimensional parameters slowly increase. Meanwhile the aspect ratio remainsalmost unchanged. Finally, in the region near the boundary the Si grain becomescoarsened with the preferred growth direction, and a few faceted Si flakes even occur.In the EAl-18Si alloy with a low eutectic undercooling of 5°C the quasi-eutectic disappears,displaying the coarse angular primary Si crystals and the partially modified eutectic Si crystal. It is apparent that theeutectic undercooling of the alloy is an important factor in determining if the quasi-eutecticstructure appears.

Fig.5.Plot of width, length and aspect ratio of eutectic Si crystal in casting and upon heat-treatment vs. Si content in HDEASAs.

Fig.6.Plot of distribution of width(A), length(B) and aspect ratio(C)of Si crystal in eutectic cell in as-cast EAl-14Si alloy (Figure 3) and after heat-treatment (Figure 10) against distance from center of eutectic cell.

Note that the EAl-15Si alloy is subjected to a considerable fading of the self-modified structure,the flaky Si crystal with an average length of about 11μm appears (Figures 4, 5). However, themicrostructure is different from that of an unmodified alloy as shown in Fig.7. As is well known,in untreated alloys the Si phase appears in the form of a large plate, which is composed of {111}multiple twins with a <112>preferred growth directions parallel to the {111} plane[46,47]. Theimportant microstructural feature is one in which that most sides and ends of thelarge plate are sharp and smooth, and on which there is no potential site to separate the plateinto several smaller segments during heat treatment [35]. By contrast, in the HDEASA Si flake(Figure 7) is characterized by the fact that it contains only a single twin system, ofwhich the twinning planes are not parallel to the growth direction, therefore the surface of the Siflake is very rough, with a lot of tips as in the Na-modified alloy [48]. Therefore, the quasi-eutecticmicrostructure would readily cause the variety of morphology upon heating, finally splitting theSi flake into several small pieces.

After heating HDEASAs with Si level ranging from 11.7wt% to 15.6wt% at 505°C -515°C for 4-8hrs the quasi-eutectic Si crystals, either self-modified or flaky (Figures 1-4), are fully or almost subjected to spheroidization (Figures 8-11).Most of sphere size range from 1.0μm to 4.0μm independent of Si content. The outline of eutectic cell remains unchanged as in casting(Fig.10), and Si nodules are well-distributed through Al-matrix. The Si sphere size slowly increases from the center to boundary of eutectic cell as indicated in Figure 6, while the aspect ratio nearly remains fixed ranging between 1.2 and 1.4. On the cell boundary Si coral grows suddenly larger, and a few of blunted polyhedra can be even observed as clearly seen in Fig.10.

Fig.9.Microstructure of EAl-13Sialloy (Fig.2) upon heat-treatment. The boundary of eutectic cell is undistinguishable. Optical.

Fig.10.SEM micrograph of EAl-14Si alloy (Fig.3) upon heating. The outline of eutectic cell, which is indicated by dotted line and surrounded with the large Si grains either nodular or angular, remains unchanged as a nodule in casting. The diameter of cell is about 100μm.The most Si nodule size ranges from 1μm to 3μm.

Fig.11.Optical micrograph of EAl-15Si alloy(Fig.4) upon soaking. The outline of as-cast eutectic cell is distinguishable.

Fig. 12.Plot of distribution of width(A), length(B) and aspect ratio(C) of Si sphere in HDEASAs upon heat-treatment.

Experimental results demonstrated that the Si content is a major factor influencing the distribution of the widths, lengths and aspect ratio of Si nodule (Figure 12), and their average values (Figure 5).It is apparent that with increase in Si content from 11.5 wt% to 14.2 wt% the size of Si grain seems to be, if any, constant. As Si level is raised to 15.6 wt%, the size significantly becomes larger. And increasing Si concentration doesn’t affect the aspect ratio, ranging from 1.2 to 1.5. In the EAl-18Si alloy the morphology of the angular primary Si crystal remains unchanged as in casting andthe partially modified eutectic Si can be granulated in a great degree. Comparing the experimental results (Fig.5, 6) it is reasonable to conclude that the refined Si crystal in casting is suitable to split into small Si coal.In addition with increase in Si level from 7wt% to 11.5wt% in hypoeutectic alloys the Si nodule number slowly decreases; meanwhile the particle volume and spacing between two neighboring Si grains insignificantly become larger (Figure 13). On the contrary, as Si content is raised from 11.5wt% to 15.6wt% in hypereutectic alloy the Si grain number suddenly drops down; its volume and spacing greatly increase.

Fig.13. Plot of volume, number and spacing of Si nodule against Si content in HDEASAs.

Fig.14.Change in volume growth rate of Si nodule with Si content.

It is obvious that Si content greatly affects the spheroidization of Si crystal, in which Si diffusion is a controlling factor rather than kinetics of Si growth [34,35].Zhu and Lui indicated that the rate of diffusion of Si atoms from high to area of low energy is proportional to Si concentration, curvature of surface of Si grains and lattice deformation energy of Si phase, and inversely to the spacing of Si grains [35,49]. In the undercooled HDEASAs there are three major factors accelerating the rate of mass transport of Si atoms in Al-matrix. The first is extension of Si solubility in Al-matrixbeyond the equilibrium[45].During heating Si atoms are readily rejected from the matrix, accelerating the diffusion rate of Si atom in Al-matrix. Secondly, one undercooling phase i.e. quasi-eutectic is formed rather than two equilibrium phases i.e. primary Si crystal and Al-Si eutectic. The most important issue is that the higher the Si content, the coarser the primary Si grain. Thus, the primary-free quasi-eutectic Si phase exhibits the higher lattice defect energy, strengthening the rate of diffusion of Si atoms in Al-matrix. Thirdly, a lot of microstructural defects (Figure 7) displaying high curvature of surface of Sigrain, increase Si diffusion rate in Al-matrix. As a result the rate of volume growth in HDEASAs is much higher than that in alloys, either hypoeutectic or eutectic. Moreover, as Si concentration is raised in HDEASAs the rate of volume growth significantly becomes larger as shown in Figure 14. That is reason why the volume of Si grain grows rapidly, accompanying with sharp decrease in number of Si grains as Si content is higher than 11.5wt% (Fig.13)although the spacing of Si grains becomes larger, reducing the rate of volume growth[35,49]. It is an advanced superiority of HDEASA in production of hypereutectic Al-Si alloy with nodular Si. In other hand it might be a drawback forthe components applied at high temperature.

(2)Achievement of the quasi-eutectic structure is most important for producing hypereutectic Al-Si alloy with completely nodular Si.

(3)The higher the Si content, the stronger the tendency to grow into large nodules.

(4)A high eutectic undercooling in freezing of alloy is a key factor in obtaining small Si spheres.

(5)Spheroidization of Si phase at lower temperatures is attributed to thermodynamic structural instability and micro-structural defect of the Si crystal, which is related to the electrolytic process in the reduction pot.